CN107326246B - A kind of high-performance high-entropy alloy and its processing method - Google Patents

A kind of high-performance high-entropy alloy and its processing method Download PDF

Info

Publication number
CN107326246B
CN107326246B CN201710583007.4A CN201710583007A CN107326246B CN 107326246 B CN107326246 B CN 107326246B CN 201710583007 A CN201710583007 A CN 201710583007A CN 107326246 B CN107326246 B CN 107326246B
Authority
CN
China
Prior art keywords
alloy
melting
plasticity
temperature
intensity
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
CN201710583007.4A
Other languages
Chinese (zh)
Other versions
CN107326246A (en
Inventor
江峰
陈良斌
唐可
杨中岳
吴亚科
孙军
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Shenzhen Biest Precision Co ltd
Original Assignee
Xian Jiaotong University
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Xian Jiaotong University filed Critical Xian Jiaotong University
Priority to CN201710583007.4A priority Critical patent/CN107326246B/en
Publication of CN107326246A publication Critical patent/CN107326246A/en
Application granted granted Critical
Publication of CN107326246B publication Critical patent/CN107326246B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon

Abstract

The invention discloses a kind of high-performance high-entropy alloy and its processing methods, by Fe40Mn40Co10Cr10The carbon of certain content is introduced in alloy, interstitial solid solution is formed with matrix, on the one hand the stacking fault energy of material can be effectively reduced, so that can induce twin at room temperature, another aspect carbon can provide additional intensity increment for matrix by solid solution and carbide precipitate.Carbon of the present invention is as good interstitial atom and carbide as effective precipitation strength phase, by being kept the temperature in final step in the higher temperature long period, as-forged microstructure is partially or completely eliminated, after part precipitation phased soln forms nearly phase structure, alloy can have again the controllable space of biggish performance on the basis of higher performance level, be conducive to further be strengthened by the combination of other schedule of reinforcements such as working hardening and precipitation strength, obtain more reasonable intensity and plasticity collocation, and the content of overall alloy element is reasonable, it is at low cost, has stronger economy.

Description

A kind of high-performance high-entropy alloy and its processing method
[technical field]
The invention belongs to the design of the ingredient of high performance alloys and treatment process field, design a kind of high-performance high-entropy alloy and Its processing method.
[background technique]
High-entropy alloy is a kind of alloy based on new alloy design concept proposed by Ye Junwei in 2004, this kind of Alloy typically contains five kinds or more of alloying element (forming there are also four kinds of elements), and every kind of constituent content is 5% More than, no clear superiority element, also there is mixed structure sometimes in generally single-phase FCC or BCC in structure.High-entropy alloy Because of its strong solid solution effect, intensity with higher, thermal stability, wearability and corrosion resistance, obtained since proposition Extensive concern and research, it is considered to be a kind of potential structural material.
But part high-entropy alloy system, such as Fe40Mn40Co10Cr10, but show that cryogenic property is excellent, and room temperature intensity has The characteristics of limit, limits the actual use of such alloy；In addition, by introducing traditional material reinforcement means, such as precipitation strength And dislocation strengthening causes the significant decrease of its plasticity, therefore although the room temperature intensity of the part high-entropy alloy can be improved It usually needs to be balanced in intensity and plasticity in practical application, significantly limits the expansion of high-entropy alloy application.Interface Strengthen, including intercrystalline strengthening and twinning strengthening, it is considered to be it can preferably coordinate a kind of means of intensity and plasticity, it is especially twin Crystalline substance is strengthened, and can increase substantially the intensity and plasticity of material simultaneously, but induces twin and then need to meet some requirements.It grinds Study carefully the doping shown through alloying element, the stacking fault energy for reducing material is a kind of feasible method.Pass through reasonable ingredient and work Skill design, it is possible to which the room-temperature property of biggish lift portion high-entropy alloy pushes its practical application.
[summary of the invention]
It is an object of the invention to solve Fe40Mn40Co10Cr10The problems such as room temperature intensity that alloy faces is insufficient, and coordinate Relationship between eager to do well in everything degree and plasticity, provides a kind of high-performance high-entropy alloy and its processing method.The present invention by Fe40Mn40Co10Cr10The carbon that certain content is introduced in alloy forms interstitial solid solution with matrix, on the one hand can effectively drop The stacking fault energy of low material, so that can induce twin at room temperature, another aspect carbon can be by being dissolved and analysing Carbide provides additional intensity increment for matrix out, effectively improves the room-temperature property of material.
In order to achieve the above objectives, the present invention is achieved by the following scheme:
A kind of high-performance high-entropy alloy, according to master alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition ingredient and carry out Melting, wherein alloy substrate Fe40Mn40Co10Cr10Middle each element atomic percentage content are as follows: Fe:35-45%；Mn:35-45%； Co:5-15%；Cr:5-15%；
Adulterate 0 < x≤10at% of content of carbon.
A further improvement of the present invention lies in that:
The crystallite dimension for the high-performance high-entropy alloy that melting obtains is 100-300 μm.
A kind of processing method of high-performance high-entropy alloy, comprising the following steps:
1) according to master alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition ingredient and carry out melting, obtain crystallite dimension Cast alloy between 100-300 μm；Wherein, 0 < x≤10at%；
2) if the quality of master alloy melting and the method for smelting of selection keep reference alloy GB/T 13298-2015 equal when sampling Even property and consistency meet the regulation of GB/T 11352-2009 and GB/T 7233, then follow the steps 3)；It is no to then follow the steps 4)；
3) by adjusting the phosphorus content of cast alloy, if practical be on active service of tensile strength and plasticity satisfaction of alloy is wanted after adjusting It asks, then adopts use；It is no to then follow the steps 4)；Wherein, practical service demand be tensile strength between 500~2000MPa and Intensity-plasticity collocation of the plasticity between 10~100% requires；
4) in vacuum annealing furnace, to step 1) obtain cast alloy between 1000-1300 DEG C homogenizing annealing 8- 24h；
5) to after homogenization alloy carry out upsetting pull processing, 1000-1100 DEG C of initial forging temperature, final forging temperature 950-1000 ℃；
6) alloy after upsetting pull is further forged in lower temperature, 900-1000 DEG C of initial forging temperature, final forging temperature 850- 900℃；
7) if the intensity and plasticity of the material after the completion of forging meet practical service demand, use is adopted；Otherwise it executes Step 8)；
8) to the alloy after the completion of forging in vacuum drying oven 850~1100 DEG C at a temperature of be heat-treated, time 10- 60min；
9) if the intensity and plasticity of alloy meet practical service demand, use is adopted；Otherwise executive termination condition judges, Processing is terminated if meeting termination condition, is discarded alloy, is otherwise returned to step 3)；
The termination condition are as follows: if the carbon content of alloy, in x=5 or 10, the intensity and plasticity of alloy pass through step 3)- 8) after processing, it is not still able to satisfy practical service demand, then terminates processing, discards alloy.
Compared with prior art, the invention has the following advantages:
The present invention effectively reduces the stacking fault energy of material, and inducing twin becomes more to be easy, meanwhile, carbon is as good Interstitial atom and carbide as effective precipitation strength phase, can greatly improve performance of the material in room temperature, fit When doping and the reasonably combined for the treatment of process performance regulation suites of measure more abundant can be provided, especially by most It is kept the temperature in step in the higher temperature long period afterwards, as-forged microstructure is partially or completely eliminated, and part is precipitated phased soln and is formed closely After phase structure, alloy can have again the controllable space of biggish performance on the basis of higher performance level, be conducive to Further strengthened by the combination of other schedule of reinforcements such as working hardening and precipitation strength, obtains more reasonable intensity It arranges in pairs or groups with plasticity, and the content of overall alloy element is reasonable, it is at low cost, have stronger economy.
[Detailed description of the invention]
Fig. 1 is the different carbon content as cast condition Fe using the small quality melting of vacuum arc furnace ignition40Mn40Co10Cr10The metallographic of alloy Tissue；
Fig. 2 is the different carbon content as cast condition Fe using the small quality melting of vacuum arc furnace ignition40Mn40Co10Cr10The stretching of alloy Performance curve；
Fig. 3 is the tissue of the ingot casting obtained using suspension smelting furnace melting；
Fig. 4 is the (Fe using suspension smelting furnace melting and Jing Guo different post-processings40Mn40Co10Cr10)96.7C3.3Alloy Tensile property curve.
[specific embodiment]
The invention will be described in further detail with reference to the accompanying drawing:
The processing method of high-performance high-entropy alloy of the present invention, comprising the following steps:
1) according to master alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition ingredient and carry out melting, obtain crystallite dimension Cast alloy between 100-300 μm；Wherein, 0 < x≤10at%；
2) if the quality of master alloy melting and the method for smelting of selection keep reference alloy GB/T 13298-2015 equal when sampling Even property and consistency meet the regulation of GB/T 11352-2009 and GB/T 7233, then follow the steps 3)；It is no to then follow the steps 4)；
3) by adjusting the phosphorus content of cast alloy, if practical be on active service of tensile strength and plasticity satisfaction of alloy is wanted after adjusting It asks, then adopts use；It is no to then follow the steps 4)；Wherein, practical service demand be tensile strength between 500~2000MPa and Intensity-plasticity collocation of the plasticity between 10~100% requires；
4) in vacuum annealing furnace, to step 1) obtain cast alloy between 1000-1300 DEG C homogenizing annealing 8- 24h；
5) to after homogenization alloy carry out upsetting pull processing, 1000-1100 DEG C of initial forging temperature, final forging temperature 950-1000 ℃；
6) alloy after upsetting pull is further forged in lower temperature, 900-1000 DEG C of initial forging temperature, final forging temperature 850- 900℃；
7) if the intensity and plasticity of the material after the completion of forging meet practical service demand, use is adopted；Otherwise it executes Step 8)；
8) to the alloy after the completion of forging in vacuum drying oven 850~1100 DEG C at a temperature of be heat-treated, time 10- 60min；
9) if the intensity and plasticity of alloy meet practical service demand, use is adopted；Otherwise executive termination condition judges, Processing is terminated if meeting termination condition, is discarded alloy, is otherwise returned to step 3)；
The termination condition are as follows: if the carbon content of alloy, in x=0.05,5,10, the intensity and plasticity of alloy pass through step Rapid 3) -8) after processing, it is not still able to satisfy practical service demand, then terminates processing, discard alloy.
1 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)97.8C2.2Composition carry out ingredient, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times, obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can guarantee ingredient and structural homogenity, and Tensile strength About 650MPa meets service demand, is not necessarily to subsequent processing, can be used directly；
Ingot structure after the alloy melting of the ingredient is as shown in Figure 1, about 100 μm of average grain size, the casting of the ingredient The stress strain curve of ingot is as shown in C2.2 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 38%；
2 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times, obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can guarantee ingredient and structural homogenity, and Tensile strength About 787MPa meets service demand, is not necessarily to subsequent processing, can be used directly；
Ingot structure after the alloy melting of the ingredient is as shown in Figure 1, about 100 μm of average grain size, the casting of the ingredient The stress strain curve of ingot is as shown in C3.3 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 67%；
3 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)95.6C4.4Composition carry out ingredient, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times, obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can guarantee ingredient and structural homogenity, and Tensile strength About 836MPa meets service demand, is not necessarily to subsequent processing, can be used directly；
Ingot structure after the alloy melting of the ingredient is as shown in Figure 1, about 100 μm of average grain size, the casting of the ingredient The stress strain curve of ingot is as shown in C4.4 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 77%；
4 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)93.4C6.6Composition carry out ingredient, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times, obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can guarantee ingredient and structural homogenity, and Tensile strength About 960MPa meets service demand, is not necessarily to subsequent processing, can be used directly；
Ingot structure after the alloy melting of the ingredient is as shown in Figure 1, about 100 μm of average grain size, the casting of the ingredient The stress strain curve of ingot is as shown in C6.6 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 104%；
5 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)91.1C8.9Composition carry out ingredient, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times, obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can guarantee ingredient and structural homogenity, and Tensile strength About 1080MPa meets service demand, is not necessarily to subsequent processing, can be used directly；
Ingot structure after the alloy melting of the ingredient is as shown in Figure 1, about 100 μm of average grain size, the casting of the ingredient The stress strain curve of ingot is as shown in C8.9 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 129%；
From small quality, the Fe of arc melting is used40Mn40Co10Cr10The organization chart 1 and stress strain curve Fig. 2 of alloy casting state As can be seen that compared with the alloy of not carbon elements, the tissue change of the alloy after doping is unobvious under preparation method of the same race, But with the raising of phosphorus content, intensity also correspondinglys increase therewith, and plasticity then shows the variation characteristic fallen after rising, and is containing Plasticity is best when carbon amounts is 3.3at%.
6 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)90C10Composition carry out ingredient, gross mass 200g or so, true Melting is carried out under empty electric arc furnaces, melting four times, obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can guarantee ingredient and structural homogenity, and Tensile strength About 1160MPa meets service demand, is not necessarily to subsequent processing, can be used directly；
7 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, is obtained the most of as cast condition between 200-300 μm of crystallite dimension and is closed Gold；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting that smelting in suspension obtains is kept the temperature for 24 hours at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, and elongation percentage about 20% is full Sufficient requirement can be directlyed adopt without post-processing；
The tissue of ingot casting by obtaining after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.The alloy of the ingredient is in the stress strain curve such as Fig. 4 after the above treatment process shown in " Forging ", It can be seen that the carbon-free Fe prepared under with method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and tensile strength is relatively free of Carbon (600MPa) improves about 83%；
8 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, is obtained the most of as cast condition between 200-300 μm of crystallite dimension and is closed Gold；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting that smelting in suspension obtains is kept the temperature for 24 hours at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 850 DEG C of temperature, time 10min；
The tissue of ingot casting by obtaining after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.Stress strain curve of the alloy of the ingredient after the above treatment process such as " 850-10min " institute in Fig. 4 Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity are all Want more excellent, especially tensile strength less carbon containing (600MPa) improves about 66%；
9 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, is obtained the most of as cast condition between 200-300 μm of crystallite dimension and is closed Gold；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting that smelting in suspension obtains is kept the temperature for 24 hours at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 950 DEG C of temperature, time 10min；
The tissue of ingot casting by obtaining after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.Stress strain curve of the alloy of the ingredient after the above treatment process such as " 950-10min " institute in Fig. 4 Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity are all Want more excellent, especially tensile strength less carbon containing (600MPa) improves about 66%；
10 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, is obtained the most of as cast condition between 200-300 μm of crystallite dimension and is closed Gold；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting that smelting in suspension obtains is kept the temperature for 24 hours at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1050 DEG C of temperature, time 10min；
The tissue of ingot casting by obtaining after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.Stress strain curve of the alloy of the ingredient after the above treatment process such as 1050-10min institute in Fig. 4 Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity are all Want more excellent, tensile strength less carbon containing (600MPa) improves about 62%, and plastic strain more carbon containing (600MPa) improves about 71%；
11 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, is obtained the most of as cast condition between 200-300 μm of crystallite dimension and is closed Gold；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting that smelting in suspension obtains is kept the temperature for 24 hours at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1100 DEG C of temperature, time 10min；
The tissue of ingot casting by obtaining after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.Stress strain curve of the alloy of the ingredient after the above treatment process such as " 1100-10min " institute in Fig. 4 Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity are all Want more excellent, tensile strength less carbon containing (600MPa) improves about 50%, and plastic strain more carbon containing (600MPa) improves about 114%；
12 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, is obtained the most of as cast condition between 200-300 μm of crystallite dimension and is closed Gold；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting that smelting in suspension obtains is kept the temperature for 24 hours at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1100 DEG C of temperature, time 30min；
The tissue of ingot casting by obtaining after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.Stress strain curve of the alloy of the ingredient after the above treatment process such as " 1100-30min " institute in Fig. 4 Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and intensity and plasticity are all Want more excellent, tensile strength less carbon containing (600MPa) improves about 50%, and plastic strain more carbon containing (600MPa) improves about 143%；
From big quality, (the Fe of suspension smelting furnace melting is used40Mn40Co10Cr10)96.7C3.3By different heat treatment systems Alloy tensile curve graph 4 can be seen that under preparation method of the same race after degree, the conjunction compared with the alloy of not carbon elements, after doping Gold can obtain higher intensity in lower temperature heat treatment, such as example in Fig. 4, can get maximum intensity about after the completion of forging 1100MPa, and with the raising of heat treatment temperature, the strength reduction of material, and plasticity improves, but generally speaking, it compares not The alloy of carbon doping is carried out, intensity and plasticity are obviously improved, should select according to practical service demand in practical application Select suitable processing technology and heat treating regime.
13 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, obtains cast alloy of the crystallite dimension at 300 μm or so；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is in 1300 DEG C of heat preservation 8h；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1100 DEG C of initial forging temperature, 1000 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 1000 DEG C of initial forging temperature, 900 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1000MPa, elongation percentage about 25%, modeling Property is poor, needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1100 DEG C of temperature, time 30min；
14 (Fe of embodiment40Mn40Co10Cr10)
It 1) is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out ingredient, gross mass 8kg or so, Melting is carried out under vacuum levitation melting furnace, melting four times, obtains cast alloy of the crystallite dimension at 300 μm or so；
2) single melting 8kg cannot be guaranteed ingredient and structural homogenity under this kind of method, need subsequent processing；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is in 1200 DEG C of heat preservation 15h；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1000 DEG C of initial forging temperature, 950 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 900 DEG C of initial forging temperature, 850 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 900MPa, elongation percentage about 25%, plasticity It is poor, it needs to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1000 DEG C of temperature, time 1h；
The principle of the present invention:
By in Fe40Mn40Co10Cr10Middle introducing interstitial element carbon reduces the stacking fault energy of material, reduces and induces twin formation Required condition, meanwhile, by the introducing of carbon appropriate, can except twinning strengthening, introduce solution strengthening and/or Precipitation strength further increases the room-temperature property of material, keeps the temperature especially by final step in the higher temperature long period, As-forged microstructure is partially or completely eliminated, and after part precipitation phased soln forms nearly phase structure, alloy can be in higher performance water Have the controllable space of biggish performance again on the basis of flat, is conducive to through other schedule of reinforcements such as working hardening and precipitation The combination of reinforcing is further strengthened, and more reasonable intensity and plasticity collocation are obtained.

Claims (1)

1. a kind of processing method of high-performance high-entropy alloy, the crystallite dimension for the high-performance high-entropy alloy that melting obtains is 100- 300μm；It is characterized in that, the processing method the following steps are included:
1) according to master alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition ingredient and carry out melting, obtain crystallite dimension exist Cast alloy between 100-300 μm；Wherein, 0 < x≤10at%；
2) uniformity when if the quality of master alloy melting and the method for smelting of selection sample reference alloy GB/T 13298-2015 3) regulation for meeting GB/T 11352-2009 and GB/T 7233 with consistency, thens follow the steps；It is no to then follow the steps 4)；
3) by adjusting the phosphorus content of cast alloy, if the tensile strength and plasticity of alloy meet practical service demand after adjusting, Then adopt use；It is no to then follow the steps 4)；Wherein, practical service demand is tensile strength between 500~2000MPa and plasticity Intensity-plasticity collocation between 10~100% requires；
4) in vacuum annealing furnace, to step 1) obtain cast alloy between 1000-1300 DEG C homogenizing annealing 8-24h；
5) to after homogenization alloy carry out upsetting pull processing, 1000-1100 DEG C of initial forging temperature, 950-1000 DEG C of final forging temperature；
6) alloy after upsetting pull is further forged in lower temperature, 900-1000 DEG C of initial forging temperature, final forging temperature 850-900 ℃；
7) if the intensity and plasticity of the material after the completion of forging meet practical service demand, use is adopted；It is no to then follow the steps 8)；
8) to the alloy after the completion of forging in vacuum drying oven 850~1100 DEG C at a temperature of be heat-treated, time 10- 60min；
9) if the intensity and plasticity of alloy meet practical service demand, use is adopted；Otherwise executive termination condition judges, if symbol It closes termination condition and then terminates processing, discard alloy, otherwise return to step 3)；
The termination condition are as follows: if the carbon content of alloy, in x=5 or 10, the intensity and plasticity of alloy pass through step 3) -8) After processing, it is not still able to satisfy practical service demand, then terminates processing, discards alloy.
CN201710583007.4A 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method Active CN107326246B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201710583007.4A CN107326246B (en) 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201710583007.4A CN107326246B (en) 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method

Publications (2)

Publication Number Publication Date
CN107326246A CN107326246A (en) 2017-11-07
CN107326246B true CN107326246B (en) 2019-02-05

Family

ID=60227248

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201710583007.4A Active CN107326246B (en) 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method

Country Status (1)

Country Link
CN (1) CN107326246B (en)

Families Citing this family (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108048724B (en) * 2017-12-19 2019-09-03 郑州大学 A kind of high-performance high-entropy alloy and its processing method
CN108213422B (en) * 2017-12-20 2020-02-11 中南大学 Preparation method of carbon-containing high-entropy alloy composite material
CN108220837A (en) * 2018-01-19 2018-06-29 北京理工大学 High-entropy alloy mismatch, which is cut, pulls out processing technology
CN108411132A (en) * 2018-05-04 2018-08-17 广西大学 A kind of preparation method of magnetic levitation vacuum melting FeMnNiCoCr high-entropy alloys
CN108439986A (en) * 2018-05-09 2018-08-24 西北工业大学 (HfTaZrTiNb) preparation method of C high entropys ceramic powder and high entropy ceramic powder and high entropy ceramic block
CN109182877B (en) * 2018-11-07 2020-12-04 北京科技大学 (NbMoTaW)100-xMxRefractory high-entropy alloy and preparation method thereof
CN110129731B (en) * 2019-05-22 2021-01-19 江苏理工学院 Anti-fatigue high-entropy alloy film and preparation method thereof
CN112522634B (en) * 2019-09-17 2021-11-09 东北大学 High-strength high-entropy alloy and preparation method thereof
CN110484796B (en) * 2019-09-20 2020-11-10 吉林大学 Transition metal carbide high-entropy ceramic particles and preparation method thereof
CN110923538B (en) * 2019-12-12 2021-06-29 燕山大学 High-entropy alloy with multidirectional annealing twin crystals and preparation method thereof
CN111636036B (en) * 2020-06-12 2022-07-22 中国矿业大学 High ferromanganese alloy and strengthening and toughening method for regulating metastable phase thereof
CN112522563B (en) * 2020-10-30 2022-03-01 西安福莱电工合金有限公司 Low-temperature high-strength high-toughness high-entropy alloy and processing method thereof
CN112725681B (en) * 2020-12-29 2022-03-15 中国矿业大学 Iron-cobalt-nickel-manganese-copper high-entropy cast iron and preparation method and application thereof
CN115491560A (en) * 2021-06-17 2022-12-20 西北工业大学 Method for improving low-temperature wear resistance of alloy
CN115354241B (en) * 2022-09-01 2023-05-12 西北工业大学 Low-temperature wear-resistant alloy with strong plasticity synergistic improvement and preparation method thereof

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002173732A (en) * 2000-11-29 2002-06-21 Univ Qinghua High entropy multicomponent alloy
CN104694808A (en) * 2015-03-26 2015-06-10 北京科技大学 High-entropy alloy with dispersion nano-sized precipitate strengthening effect and preparing method thereof
JP2016023364A (en) * 2014-07-25 2016-02-08 株式会社日立製作所 Alloy structure
CN106756407A (en) * 2016-12-07 2017-05-31 徐轶 A kind of CrMnFeCoNiZr high-entropy alloys and preparation method thereof

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002173732A (en) * 2000-11-29 2002-06-21 Univ Qinghua High entropy multicomponent alloy
JP2016023364A (en) * 2014-07-25 2016-02-08 株式会社日立製作所 Alloy structure
CN104694808A (en) * 2015-03-26 2015-06-10 北京科技大学 High-entropy alloy with dispersion nano-sized precipitate strengthening effect and preparing method thereof
CN106756407A (en) * 2016-12-07 2017-05-31 徐轶 A kind of CrMnFeCoNiZr high-entropy alloys and preparation method thereof

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
Design of a twinning-induced plasticity high entropy alloy;Y.Deng et al.;《Acta Materialia》;20150516(第94期);第124-125页
Effect of carbon content and annealing on structure and hardness of the CoCrFeNiMn-based high entropy alloys;N.D.Stepanov et al.;《Journal of Alloys and Compounds》;20160611(第687期);第59-60页

Also Published As

Publication number Publication date
CN107326246A (en) 2017-11-07

Similar Documents

Publication Publication Date Title
CN107326246B (en) A kind of high-performance high-entropy alloy and its processing method
CN108251760B (en) The martensitic stain less steel and its manufacturing method of the mutually compound precipitation strength of nanometer
CN105568151B (en) A kind of aluminium enhancing Maraging steel and preparation method thereof
CN101538686B (en) Martensite precipitation hardening stainless steel for structural member and manufacturing method thereof
CN107557667A (en) A kind of large die-casting mould high performance hot-work die steel and its manufacturing process
CN109338160A (en) The castable forging solid solution tungsten alloy of one kind and preparation method
CN104630597B (en) A kind of iron nickel and chromium high temperature alloy and its manufacture method
CN104745879B (en) High-density ultra-strength Co strengthens Ni-based high tungsten heat-resisting alloy and preparation method
CN112522645B (en) Preparation method of high-strength high-toughness homogeneous fine-grain CrCoNi intermediate-entropy alloy thin plate
CN110484812A (en) A kind of high-performance hot stamping die steel and its manufacturing process
CN104233003B (en) A kind of high manganese nichrome resistance electrothermal alloy and preparation method thereof
CN110157970A (en) A kind of high strength and ductility CoCrNi medium entropy alloy and preparation method thereof
CN105821250A (en) High-strength nickel-base superalloy and manufacturing method thereof
CN104745880B (en) A kind of high density kinetic energy superhigh intensity tungsten nickel heat-resisting alloy and preparation method
CN105088017A (en) Double-phase high-density kinetic energy tungsten-nickel-cobalt alloy capable of being cast and forged and preparation method
CN108220807A (en) A kind of low-density high alumina superelevation carbon bearing steel and preparation method thereof
CN110218948A (en) A kind of low-density high tenacity steel and preparation method thereof
CN109136765A (en) A kind of hot die steel and preparation method thereof
CN109112425A (en) A kind of ultrahigh-intensity high-toughness Maraging steel and its preparation method and application
CN112301255A (en) High-thermal-conductivity and high-strength Co-Fe-Ni alloy for die and additive manufacturing method thereof
CN106702241A (en) Boron strengthened high-density and high-strength tungsten, nickel and cobalt alloy and preparation method
CN114351058B (en) Alloy steel with yield strength of 2000MPa and preparation method thereof
CN106834931A (en) A kind of hot die steel of thermal fatigue resistance and preparation method thereof
CN104711459A (en) High-density ultrahigh-strength tungsten-cobalt heat-resistant alloy and preparation method thereof
CN1009010B (en) cobalt-free nickel-based alloy

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant
TR01 Transfer of patent right

Effective date of registration: 20230608

Address after: 518127, 2nd Floor A, No. 116 Xiangshan Avenue, Luotian Community, Yanluo Street, Bao'an District, Shenzhen City, Guangdong Province

Patentee after: SHENZHEN KADAM TECHNOLOGY CO.,LTD.

Address before: Beilin District Xianning West Road 710049, Shaanxi city of Xi'an province No. 28

Patentee before: XI'AN JIAOTONG University

TR01 Transfer of patent right
TR01 Transfer of patent right

Effective date of registration: 20240312

Address after: 518000 201 Xiangshan Avenue, Luotian community, Yanluo street, Bao'an District, Shenzhen City, Guangdong Province

Patentee after: SHENZHEN BIEST PRECISION Co.,Ltd.

Guo jiahuodiqu after: Zhong Guo

Address before: 518127, 2nd Floor A, No. 116 Xiangshan Avenue, Luotian Community, Yanluo Street, Bao'an District, Shenzhen City, Guangdong Province

Patentee before: SHENZHEN KADAM TECHNOLOGY CO.,LTD.

Guo jiahuodiqu before: Zhong Guo

TR01 Transfer of patent right